Twist drawn wire

ABSTRACT

This invention comprehends torsional strengthening of two-phase metal materials. One application of the torsionally strengthened material is in the field of springs wherein the energy storage capacity is increased. The invention provides for methods and processes for increasing the torsional strength of two-phase metal materials. Also comprehended is an apparatus that provides the increased torsional strength by its novel combination of machines.

United States Patent Geary May 13, 1975 [54] DRAWN OTHER PUBLICATIONS {75] Inventor: Arthur L. Geary, Barrington, Ill,

u Toth et al., Dlrectional Properties of a Modified 5% [73] Asslgnee: Brunswlck Corporalmni skoklev Cr tool Steel" Transactions of ASM Vol. 55, 1962.

[22] Filed: Feb. 21, 1973 [21} APPL 334,223 Primary ExaminerL. Dewayne Rutledge Assistant Examiner(). F. Crutchfield Attorney, Agent, or Firm-J0hn G. Heimovics; Donald [52] US. Cl. 148/32; 29/183; 29/193; 3 Olexa; Sheldon Epstein 148/36; 148/38; 148/39 [51] Int. Cl. C22c 41/00 [58] Field of Search 29/193, 183; 148/31. 32, [57] ABSTRACT This invention comprehends torsional strengthening of [56] References Cited two-phase metal materials. One application of the tor- UNITED STATES EN sionally strengthened material is in the field of springs l 525 730 2/|925 Gates 0 138/177 X wherein the energy storage capacity is increased. The 3/1930 Miner h v A I I u 72/64 invention provides for methods and processes for in- 2,250,610 7/1941 Simons .1 72/6 X creasing the torsional strength of two-phase metal ma- 3,038,592 6/1962 Kelday et a1 l l t 4 72/64 x terials. Also comprehended is an apparatus that pro- 3,158 258 11/1964 Kelday et al...... 29/193 X vides the increased torsional strength by its novel 3,698,963 lO/l972 NUl'lCS fit Bl l l t 1, 29/196 X cumbinafion of machines FOREIGN PATENTS OR APPLICATIONS United Kingdom 29/193 13 Claims, 2 Drawing Figures TWIST DRAWN WIRE BACKGROUND OF THE INVENTION l. Field of the Invention This invention relates to improved torsional characteristics of metals and a process and apparatus for strengthening metals, and more particularly, relates to metal wire with superior torsional yield strength, and a process and an apparatus for increasing the torsional yield strength characteristic of metals.

2. Background of the Invention Twisting of wires to form a cable is well known in the wire drawing art; drawing a plurality of twisted wires through a die is also well known. In US. Pat. No. 2,250,6l0, it has been suggested to draw a single wire through a die or series of dies while twisting the wire and causing a back tension thereon. In addition, increase in corrosion resistance in stainless steel spring material is taught in British Pat. No. 722,427; precipitation of carbides in stainless steel is taught in US. Pat. No. 2,549,468; a method of increasing the tensile strength ofa special type of 18-8 stainless steel is taught in US. Pat. No. 2,795,5l9 and an article entitled High-Strength Stainless Wire And Strip Made of Iron Chromium Nickel Based Alloys" by M. N. Reavskaya in the magazine Steel in the USSR; a method of heat treating a modified percent chromium tool steel is discussed on pages 420428 in the 1962 TRANSACTIONS OF THE ASM; and special dies, rollers, and devices for changing the strength characteristics of metals are taught in U.S. Pat. Nos. 300,741; 1,525,730; 1,749,67l; l,967,487; 367,733; 3,033,592 and 3,l58,258. In fact, many different proposals have been presented, including the ones mentioned above, to mechanically work metal strips or wires in order to increase tensile strength thereof. However, the torque transmitting ability (torsional strength) of metal wire, such as required in springs, is of great significance and greater increase in torsional strength of wires used for such products is highly desir able but not recognized nor satisfactorily achieved by this prior art.

SUMMARY OF THE INVENTION This invention relates to improved torsional strength in metals and is concerned with a new and improved use of a two-phase metal structure which has improved torsional characteristics that are provided by a special process developed on a new machine combination. This invention not only recognizes but achieves increased torsional strength in metal wires that can be utilized in making superior springs, torque transmitting materials, etc.

It is therefore an object of this invention to provide a metal with increased torsional yield strength without substantially altering the tensile strength thereof.

It is another object of this invention to provide a method for increasing the torsional yield strength of metals.

Yet another object of the invention is to provide a machine combination that can provide an increase in torsional yield strength of a wire.

And yet another object of this invention is to provide a spring that exhibits increased energy storage characteristics.

DESCRIPTION OF THE DRAWINGS FIG. I is a pictorial representation of one embodi- 0 ment of the invention; and,

FIG. 2 is a cross-section of the wire and drawing die used in the embodiment of this invention of FIG. 1.

DESCRIPTION OF THE PREFERRED EMBODIMENTS This invention comprehends as a preferred embodiment a two-phase metal wire that has been either cold worked, heat treated and cold worked, or heat treated to provide at least one of the two phases in an elongated fiberized configuration. The wire is then addi tionally drawn and simultaneously twisted in the reducing portion of a drawing die, and thus, exhibits an improved torsional yield strength compared to a wire of similar composition and cold work level that has not been die twisted. In addition, it has been found that the tensile strength of such a die twisted material exhibits substantially the same or a slightly lower tensile strength when compared to a similar non-die twisted wire.

Prior to the die twisting operation, the metal wire may be fiberized by processes such as drawing, swaging, rolling, heat treating, casting, etc.. wherein the crystalline microstructure takes on an elongated fibered appearance that is parallel to the direction of the axis of the wire. This basic fiberizing can occur in either one or two phases of a two-phase material. During the die twisting operation the wire is pulled through a drawing die that reduces or constricts by plastic deformation the diameter of the wire within the reducing portion of the die only. At the same time, the wire is twisted prior to entering the die in such a fashion that only that portion of the wire that is being plastically deformed in the reducing portion of the die attains a permanent twist as it exits the die. In other words, quite surprisingly, it has been found that substantially all twisting of the wire must take place in the plastic region within the reducing portion of the die or the wire will have unstable, over and under twisted, portions along the length thereof. It is believed that the die twisting phenomena that occurs in the die results because the wire material is under plastic deformation or constriction in the one confined area.

Another embodiment of this invention is the method of increasing the torsional yield strength and, obviously, the ultimate torsional strength of a two-phase metal wire. After a metal wire is fiberized, the wire is placed on a spool which is arranged within a rotating yoke that imparts twist to the wire as it is being unspooled. Simultaneously, as the wire is unspooled, it passes through a drawing die that reduces the crosssectional area of the wire, preferably ranging from 56: to 25 percent, and more preferably, ranging from 10 to 20 percent. The wire is reduced in cross-sectional area in the reducing portion of the die and concomitantly twisted. The helical twist angle is from about 5 to about 60 and more preferably from about 40 to about 50. The twist is set in the wire also in the reducing portion of the die while the material is plastically flowing. As the wire exits the die, twist arrest rolls prevent over twist or under twist so that the wire is uniformly twisted and no unstable portions are formed along the length of the wire. If an unstable portion existed. then localized fracture would occur. The fiberizing operation depends upon the type of metal being used and can occur in metals undergoing diffusionless transformation which may be brought about by cold work or diffusion control transformations brought about by heat treatment. For example, materials having two phases wherein one phase is harder than the other and created by diffusionless transformation are: (1) beta titanium having a soft beta phase and a harder omega phase; (2) beta zirconium having a soft beta phase and a harder omega phase; (3) type l8-8 stainless steels having a soft austenite phase and a harder martensite phase; and (4) gamma uranium having a soft gamma phase and a hard gamma prime phase. Examples of diffusion transformations wherein two phases exist are found in metals including (1) medium and (2) high carbon steel having a soft ferrite phase and a harder pearlite phase; (3) silver-copper alloys having a soft silver phase and a harder copper phase; (4) silver-nickel alloys having a soft silver phase and a harder nickel phase; and, (5) aluminum-beryllium alloys having a soft aluminum phase and a harder beryllium phase. Alternatively, it is believed that other forms of producing fiberized characteristics in wire material other than by cold work and heat treatment can be employed, such as by controlled directional solidification. This process can be adapted to provide a helical fiberized structure.

It has been found that when an 18-8 stainless steel such as that described in US. Pat. No. 3,698,963 has been not only cold worked but twist drawn on the last pass through a drawing die or even twist drawn and then finally reduced in a sizing die, that the helical disposition of the fiberized martensite phase results in improved ductility, fatigue life and fracture strength of the stainless steel. In other words, by combining the invention hereof with the teachings of US. Pat. No. 3,698,963 not only can the tensile strength of 18-8 stainless steel exceed 400,000 psi, but the ductility, fatigue life and fracture strength thereof are significantly improved, thus making this ultra high strength stainless steel an im roved spring material.

When working with the type 18-8 stainless steel, it has been found that when volume fractions of martensite are less than 50 percent. residual stresses and work hardening due to torsional prestraining principally control the strengthening response due to die twisting. it has also been found that at volume fractions of martensite greater than 50 percent, the orientation of the harder phase strongly influences the strengthening response due to die twisting. Strengthening due to orientation is not only true for the l8-8 stainless steels, but for all the two-phase type metals. When dealing with type 18-8 stainless steel metals and, in fact, all the twophase metals, once an appropriate strength level or the basic range of strength level has been obtained, either by thermo-mechanical treatment, cold working or heat treatment, die twisting of the wire or rod is performed in order to increase its preselected torsional strength properties. This occurs by orienting theh fiberized metallographic microstructure of the metal wire in a helical configuration with respect to the axis of the wire. It has been found necessary that at least l5 percent of the harder of the two phases be present in the wire or only minimal torsional strengthening will occur. When type 18-8 stainless is being torsionally strengthened, it has been found desirable to have the wire contain at least 20 percent martensite. lf strictly cold drawing is applied, it has been found desirable with the diffusionless transformation materials, such as stainless steel, to have at least percent cold work or a 75 percent reduction in area by cold work imparted into the metal prior to the die twisting operation, The die twisting operation can involve a single or a multiple reduction pass of 5 to 30 percent, preferably the reduction will be 10 to 20 percent per pass while the wire is simultaneously being twisted.

[t is further contemplated that after die twisting occurs a final sizing pass can be utilized wherein the cross-sectional area of the wire is reduced about 10 percent or less and preferably about 5 percent or less. Although die drawing is the preferred method of cold working the wire, other methods or combinations of methods as discussed above can also be appropriately used.

In addition to a wire, the material that can be torsionally strengthened can have the configuration of a rod, strip, thin flat strip, semi-flat strip, tube or any regular (i.e. square, circular, hexagonal, l-shaped, H-shaped) or irregular (i.e. C-shaped, angle-shaped, an axis of symmetry of one) cross-sectional configuration, as desired. Any suitable process known to those skilled in the art may be adopted wherein constriction and twisting occur simultaneously within the metal working portion thereof.

In all cases it has been found necessary that an elongated fiberized microstructure exist so that the fibers during the die twisting operation may be increased in length due to the drawing operation as well as the twisting operation. Thus, the fiberized microstructure of the die twisted wire gives an appearance where the fiberization is helically twisted with respect to the axis of the wire, and the fibers are longer in length than prior to die twisting.

It has been found that by varying the annealing temperature of type 18-8 stainless steel wire prior to any cold working, it is possible to control the stability of the stainless steel for both conversion to martensite from austenite and influence torsional yield properties obtained from the die twisting operation. It is possible to affect the hardness of the final martensite phase of type 18-8 stainless steel that has been formed by cold working and die twisting. it has also been found that the carbon content has an effect on the hardness of the martensite when the material is die twisted such that the torsional yield strength increases as the carbon content of the type 18-8 stainless steel increases.

In a preferred embodiment of the invention the dietwisting apparatus is shown in FIG. 1. A yoke 52 having a back stabilizing shaft 51 and a front tubular shaft 55 is supported by bearings 53. A prime mover 50 (which can be a variable speed motor) which is coupled to the back shaft 51 of the yoke 52 by shaft 50a provides rotational motion for the yoke 52. Yoke 52 contains a payoff spool 54 that has a core 56 and side flanges 58. The spool 54 is pivotally mounted in the flange plates 59 which comprise part of the yoke 52. The spool 54 is shown as overwrapped by coiled metal wire 40. At one end of the spool 54 is an adjustable back tension friction clutch 62 that provides for the proper back tension on the wire 40. The tubular front yoke 55 also serves as a wire guide. The spool 54 is mounted approximately normal to the rotational axis of the yoke 52 defined by the center line of shafts SI and 55 thereby enabling the wire 40 to be pulled from the payoff spool 54 and aligned axially with the axis of drawing die 70. A twist arrestor 80 is located as close as possible to the exit end 7) of the drawing die 70. This aids in preventing any twist in the wire from occuring after it passes through the die 70. The arrestor 80 comprises at least a pair of spring loaded wheels 82 that squeeze or hold the wire tightly during the drawing-twisting operation. Many materials such as rubber, plastic, and metal can be successfully used; however, the wheel material and the spring force thereon will vary with the type of wire being drawn and its hardness. After the wire 40 passes through the twist arrestor 80 it is coiled on take-up spool 84 in a conventional manner. The twist arrestor rolls 82 are used to keep the wire 40 from overtwisting after it leaves the die 70, thereby confining the twist in the reducing Zone of the die 70 and at the same time preventing an unstable Zone to occur between the exit portion 71 of the die 70 and the take-up spool 84. in a wire drawing operation, the drawing die must be lubricated and therefore does not offer sufficient resistance with regard to preventing twists in the area between the die 70 and the take-up spool 84. Even by putting the take-up spool 84 close to the exit end of the die 70, the problem of twisting still occurs in that unstable areas can form partially around the take-up spool 84 where overtwisting can occur. Without the twist arrestor rolls 82 non-uniform twist occurs in the wire, thereby making an unsatisfactory product.

ln FIG. 2, a segmented portion of wire 40 is shown passing through a segmented section of die 70. The die 70 comprises an entrance portion 74; a reducing portion 72 wherein the actual wire is reduced in diameter and also twisted, and a relief portion 76. The entering wire portion 4] is shown with pictorialized fibers 42 that are parallel to the axis of the wire 40. As the constricted and twisted portion 43 leaves the die 70 the twisted and elongated fibers that were designated 42 now appear as fibers 44 and are helical with respect to the axis ofthe wire 40. In the reducing portion 72 of the die 70 these elongated fibers 42 are being twisted as depicted as intermediate fibers 45. Thus, it may be seen that as the wire 40 is pulled through the die where plastic deformation enables both constriction and twisting or torsion to occur simultaneously transforming parallel fibers to helical fibers. It should also be noted that although the twist is imparted by the yoke 52 rotating normal to the spool 54, the fiber lines on the wire are not twisted or helically wrapped until the wire enters the reducing portion '72 of the die 40 and is plastically deformed therein. Thus, both constriction and torsion take place within the reducing portion of the die simultaneously.

The payoff spool rotational speed, the linear speed of the wire being drawn at the die exit and the outer twist angle of the wire are inter-dependent variables of the twist drawing process. To achieve a specific twist (TPl) many combinations of payoff spool rotational speed and drawing speed are possible.

ln the single pass wire twisting operation and as discussed herein, all twists in the wire will be understood to mean a uniformly applied twist which is set in the wire substantially within the reducing section of the die. The twist is referred to in turns per unit length, usually turns per inch, or TPI, and is measured as the twistdrawn wire exits from the die. When twisting wire, the technique used for determining the amount of twist that is impressed in the wire consists of measuring the RPM of the spool twisting head or yoke 52. and the RPM of the drawing capstan or takeup spool 84. The diameter of the capstan 84 is easily obtained; therefore, the line speed of the wire exiting the die can easily be calculated. Impressed twist is the quotient of RPM and linear speed (inches per minute) of the exiting wire. In this analysis, it is assumed that all the applied twist is set in the wire substantially within the die and no slippage through the die occurs.

In multiple pass wire twisting operations, an initial die twist is first set in the wire and then followed by one or more single pass wire twisting operations which can be repeated, as desired.

Multiple or incremental twisting, such as referred to hereinabove, would obviously allow for die twisting to large helix angles at fast wire drawing speeds due to the smaller amount of package rotation and twist per pass.

The twist angle imparted during the die twisting oper ation may be characterized by either TPl (turns per inch) or the helix angle 01. These two parameters are related as follows:

Tan 11 Zn'r (TPl) wherein.

r is the wire radius or is the helix angle at the wire surface with respect to the wire axis; and, TP! is turns per inch. For a helix angle of 45, the TPl is inversely proportional to the wire or rod diameter, a;

l I Pl 1 mi The following examples of wire products are intended only to illustrate the invention and not limit the scope thereof in any way.

EXAMPLE I TPl 'lorsional Tensile (turns per Yield Strength Yield Strength inch l psi psi 0 l33.()UU(c 260.0001 c I 2% l4h,UOU(ct)** 252.U(ltl(ctl 5 l82,l)()ll(ct)* 222 U(|U(cti" '(c) designates material reduced in size sulel v by constriction (cit designates material reduced in size by both cnnslrlction and torsion EXAMPLE ll A type 18-8 stainless steel 0.257 inch diameter wire having a chemical composition the same as Example I was annealed at I8UOF at a rate of 2 seconds per mil.

7 The wire was cold worked to 0.1 l4 inch, 0.09] inch, 0.064 inch and 0.060 inch diameters which reflected 80%, 87.3%, 93.8% and 94.5% respectively, reductions in areas from the original 0.257 inch wire diameter. The following physical properties were measured for each diameter:

Cold Torsional Tensile Diameter TPl Work Yield Strength Yield (lnchesl l l psi Strength psi 0.] l4 30% l2l,000(c) 249,()00[c| U. I l4 3 93.3% l37.000(ct) 24100001} 0.09! 0 87.3% 1l1.l)()0(e) 29l.000(e| 0.09! 3.5 45.4% l43,000(ct) 263.000fct) 0.064 0 93 8% l3'-J [l(J0(c) 3| l,U()(J(c) 0.064 5 97.8% l55 [l00( ct) 3U0,(]00( CI) 0.060 0 94.5% 149.000(c) 296,000t'c) 0.060 4.5 97.1% 169,000(ctl 28U,000(ct) EXAMPLE Ill A type l8-8 stainless steel 0.257 inch diameter wire having a chemical composition the same as Example I was annealed at i950F at a rate of 2 seconds per mil. The wire was cold worked to 0.091 inch and 0.064 inch diameters which reflected 87.6 and 93.8 percent respectively, reductions in areas from the original 0.257 inch wire diameter the following physical properties were measured for each diameter:

Torsional Tensile Diameter Cold Yield Yield llnches) TPl Work' Strength psi Strength psi 0.09] O 87.6% 1l2,000(cl 279.000(c) 0.09l |.li 92.6% l40,000(ct) 257.000( Ct) 009] 3.5 95.4% l5 LOUUMI) ZSFLOUOHJI] 0,064 O 93.8% l43. l00() 282,000(C) 0.064 5 97.8% l7 1 (100((21) 276,000tct} Footnote. includes surface cold work due to die-twisting EXAMPLE IV A high carbon heat treated steel wire having a general chemical composition by weight of: carbon 0.88%; manganese 0.37%; phosphorus 0.008%; sulphur 0.0l2%; silicon 0.210% and remainder iron was cold worked to a 0.1 14 inch diameter. The following physical properties were measured:

Torsional Tensile Helix Yield Strength Yield Strength TPl Angle psi psi 0 O 120,0U0(cl 216,000(c] 2 36 M10001 ctl 207,000(ct) 2V2 42 l34,0UO(ct) l5b,U()(1(Ct) creases the physical properties of wires when they are to be used in torsional applications.

it was found from these examples that the torsional yield strength of wires exhibited up to 50 percent greater strength when tested in the direction of torsional prestraining or twist, as opposed to testing in the direction opposite to torsional prestraining or twist. In each example it was determined that the volume fraction of martensite was greater than 50 percent and that the material contained more than 0.06 weight percent of carbon; therefore, the orientation of the harder phase, martensite, strongly influenced the strengthening response of the material. This was to be expected, as it has been found characteristic in all two-phase materials, that the harder of the two phases when present in volume fractions of 50 percent or more strongly ini'luence the strengthening response of the metal.

The heat treated and cold drawn high carbon samples of Example IV confirm that the characteristic of the increased torsional yield strength is present in all twophase metals and that the mechanism, cold work and- /or heat treatment, only depends on the type of metal to be used.

When a wire with increased torsional strength is formed into springs, it has been found that there is increased energy storage capacity of the spring. This increased energy storage in the springs can be expected and is evidenced by Example V as described hereinafter.

EXAMPLE V Wire Characteristics Spring Characteristics Spring Wire Size Cold Spring Active No. inches Work TPI Diameter Coils A 0.0324 0 .43 6 B 00324 85% l .43 6 C 00324 85% 4 /1 .43 6 D 0.0324 85% 9 .43 6

The energy storage level for each spring was measured and the percentage increase in energy storage was found to be:

a. Spring B displayed a 31% increase over Spring A b. Spring C displayed a 38% increase over Spring A c. Spring D displayed a 66% increase over Spring A.

From Example V it can be easily recognized that when die-twisting is applied to all two-phase metals comprehended herein, including ultra high strength type l8-8 stainless steels, of 400,000 psi or more, that torsional properties, including fatigue life, can significantly be increased.

Therefore, standard spring design technology cannot be applied to springs described herein because the torsional yield strength greatly exceeds the strength relationships of standard spring material.

Although specific embodiments of the invention have been described, many modifications and changes may be made in the compositions of metals and yet still are contemplated herein. the exact method of die-twisting can be altered by substituting rolling, swag'mg. or casting processes, and the machinery can be modified without departing from the spirit and the scope of the invention, as defined in the appended claims.

I claim:

I. An anisotropic wrought two-phase metal material comprising:

a. a cold deformed uniformly fiberized metallographic microstructure being in a helical angled configuration with respect to the longitudinal axis of the material;

b. at least percent of one of the two phases being present in the material;

c. at least one of the phases present appearing as elongated fibers within the material;

and further characterized for a given reduction in cross-sectional area wherein:

l. the torsional yield strength of the material subjected to constriction and torsion is greater than the torsional yield strength of the material subjected solely to constriction, and

2. the tensile yield strength of the material subjected solely to constriction is equal to or greater than the tensile yield strength of the material subjected to constriction and torsion.

2. An anisotropic wrought two phase metal comprising:

a. a cold deformed uniformly fiberized metallographic microstructure being in a helical angle configuration with respect to the longitudinal axis of the material;

b. at least 15 percent of one of the two phases being present in the material;

c. at least one of the two phases appearing as elongated fibers within the material;

and characterized that for a given reduction in crosssectional area wherein:

l. the torsional yield strength of the material subjected to constriction and torsion is greater than the torsional yield strength of the material subjected solely to constriction.

2. the tensile yield strength of the material subjected solely to constriction is equal to or greater than the tensile yield strength of the material subjected to constriction and torsion;

d. and further characterized that when diffusionless control transformation can occur within the metal it is selected from one or more of the following groups:

type l8-8 stainless steel, bb. beta titanium, cc. beta zirconium alloys, and dd. gamma uranium alloys and when a diffusion controlled transformation occurs within the metal it is selected from one or more of the following groups consisting of:

cc. medium carbon steel.

ff. high carbon steel,

gg. silver-copper alloys,

hh. silver-nickel alloys, and ii. aluminum-beryllium alloys.

3. The material of claim 1 wherein the helical angle of the fiberized microstructure ranges from about 5 to about 4. The material of claim 1 wherein the helical angle of the fiberized microstructure ranges from about 40 to about 50.

5. The material of claim 1 wherein the torsional yield strength of the constricted and twisted material when tested in the direction of the helix angle is greater than the torsional yield strength of the material when tested in a direction opposite to the helix angle.

6. The material of claim 1 wherein the composition is that of type [8-8 stainless steel having at least a 20% martensitic structure.

7. The material of claim 1 wherein the material has a wire configuration.

8. The material of claim I wherein the material has a tubular configuration.

9. The material of claim 1 wherein the material has a strip configuration.

10. The material of claim 1 wherein the material has a regular cross-sectional configuration.

11. The material of claim 1 wherein the material has an irregular cross-section configuration.

12. An anisotropic wrought two-phase metal material characterized by having the properties of:

et c;

b. SC 2 S wherein 1. T is the torsional yield strength in psi of the material having a cold worked reduction in crosssectional area of X percent induced by constriction and torsion, said material designated as cr;

2. T is the torsional yield strength in psi of the same material having a cold worked reduction in cross-sectional area of X percent induced solely by constriction, said material designated as c;

3. S is the tensile yield strength in psi of the material cr; and

4. S is the tensile yield strength in psi of the material c; and,

c. at least l5 percent of the harder of the two phases being present in the material and further characterized in that the two phases appear in an elongated fiberized configuration as exhibited by a helical longitudinal metallographic microstructure of the metal.

13. The material of claim 12 wherein the material is an l8-8 stainless steel and the harder phase is martenslie. 

1. AN ANISOTROPIC WROUGHT TWO-PHASE METAL MATERIAL COMPRISING: A. A COLD DEFORMED UNIFORMLY FIBERIZED METALLOGRAPHIC MICROSTRUCTURE BEING IN A HELICAL ANGLED CONFIGURATION WITH RESPECT TO THE LONGITUDINAL AXIS OF THE MATERIAL; B. AT LEAST 15 PERCENT OF ONE OF THE TWO PHASES BEING PRESENT IN THE MATERIAL; C. AT LEAST ONE OF THE PHASES PRESENT APPEARING AS ELONGATED FIBERS WITHIN THE MATERIAL; AND FURTHER CHARACTERIZED FOR A GIVEN REDUCTION IN CROSSSECTIONAL AREA WHEREIN:
 1. THE TORSIONAL YEILD STREMGTH OF THE MATERIAL SUBJECTED TO CONSTRUCTION AND TORSION IS GREATER THAN THE TORSIONAL YEILD STRENGTH OF THE MATERIAL SUBJECTED SOLELY TO CONSTRUCTION, AND
 2. THE TENSILE YEILD STRENGTH OF THE MATERIAL SUBJECTED SOLELY TO CONSTRICTION IS EQUAL TO OR GREATER THAN THE TENSILE YEILD STRENGTH OF THE MATERIAL SUBJECTED TO CONSTRICTION AND TORSION.
 2. the tensile yield strength of the material subjected solely to constriction is equal to or greater than the tensile yield strength of the material subjected to constriction and torsion.
 2. An anisotropic wrought two phase metal comprising: a. a cold deformed uniformly fiberized metallographic microstructure being in a helical angle configuration with respect to the longitudinal axis of the material; b. at least 15 percent of one of the two phases being present in the material; c. at least one of the two phases appearing as elongated fibers within the material; and characterized that for a given reduction in cross-sectional area wherein:
 2. Tc is the torsional yield strength in psi of the same material having a cold worked reduction in cross-sectional area of X percent induced solely by constriction, said material designated as c;
 2. the tensile yield strength of the material subjected solely to constriction is equal to or greater than the tensile yield strength of the material subjected to constriction and torsion; d. and further characterized that when diffusionless control transformation can occur within the metal it is selected from one or more of the following groups: aa. type 18-8 stainless steel, bb. beta titanium, cc. beta zirconium alloys, and dd. gamma uranium alloys and when a diffusion controlled transformation occurs within the metal it is selected from one or more of the following groups consisting of: ee. medium carbon steel, ff. high carbon steel, gg. silver-copper alloys, hh. silver-nickel alloys, and ii. aluminum-beryllium alloys.
 3. The material of claim 1 wherein the helical angle of the fiberized microstructure ranges from about 5* to about 60*.
 3. Sct is the tensile yield strength in psi of the material ct; and
 4. Sc is the tensile yield strength in psi of the material c; and, c. at least 15 percent of the harder of the two phases being present in the material and further characterized in that the two phases appear in an elongated fiberized configuration as exhibited by a helical longitudinal metallographic microstructure of the metal.
 4. The material of claim 1 wherein the helical angle of the fiberized microstructure ranges from about 40* to about 50*.
 5. The material of claim 1 wherein the torsional yield strength of the constricted and twisted material when tested in the direction of the helix angle is greater than the torsional yield strength of the material when tested in a direction opposite to the helix angle.
 6. The material of claim 1 wherein the composition is that of type 18-8 stainless steel having at least a 20% martensitic structure.
 7. The material of claim 1 wherein the material has a wiRe configuration.
 8. The material of claim 1 wherein the material has a tubular configuration.
 9. The material of claim 1 wherein the material has a strip configuration.
 10. The material of claim 1 wherein the material has a regular cross-sectional configuration.
 11. The material of claim 1 wherein the material has an irregular cross-section configuration.
 12. An anisotropic wrought two-phase metal material characterized by having the properties of: a. Tct > Tc; b. Sc > or = Sct; wherein
 13. The material of claim 12 wherein the material is an 18-8 stainless steel and the harder phase is martensite. 